WO2020169014A1 - Yb微合金化的AI-Li合金 - Google Patents

Yb微合金化的AI-Li合金 Download PDF

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WO2020169014A1
WO2020169014A1 PCT/CN2020/075645 CN2020075645W WO2020169014A1 WO 2020169014 A1 WO2020169014 A1 WO 2020169014A1 CN 2020075645 W CN2020075645 W CN 2020075645W WO 2020169014 A1 WO2020169014 A1 WO 2020169014A1
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alloy
hardness
microalloyed
aging
content
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高坤元
聂祚仁
黄晖
文胜平
吴晓蓝
程璐
田东辉
丁宇升
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Beijing University of Technology
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Beijing University of Technology
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Priority claimed from CN201910746560.4A external-priority patent/CN110438376A/zh
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent

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  • the invention relates to a Yb microalloyed Al-Li alloy and belongs to the technical field of alloy materials.
  • Aluminum-lithium alloy has a very broad application in the aerospace field. Due to its low density, high elastic modulus, high specific strength and excellent fatigue performance, it has a very good development and application prospects. Since the aluminum-lithium alloy is a heat-treatable strengthening alloy, the AL3Li metastable phase with the L12 structure dispersed and precipitated during the heat treatment process has a very obvious strengthening effect. Since the maximum solid solubility of Li in aluminum is 4.2wt.%, a relatively large volume fraction of Al3Li phase can be precipitated during the aging process, which significantly improves the strength of the alloy.
  • the further alloying of the AL-Li alloy is particularly important.
  • the 1420 alloy of the Al-Mg-Li series is the lowest density aluminum-lithium alloy.
  • Sc element is expensive, which limits its industrial application, while Yb and Sc elements have similar properties, can precipitate a stable Al3M phase with L12 structure, and improve the strengthening effect of the alloy.
  • Yb element has a higher nucleation rate and diffusion rate, and the price of Yb element is relatively cheap, which is only one-thirtieth of Sc element. Therefore, in the present invention, the elements of Mg, Li, and Yb are compounded to obtain an alloy with low cost and good aging strengthening effect.
  • the purpose of the present invention is to provide a Yb microalloyed Al-Li alloy, which has low production cost and can produce good aging strengthening effects.
  • the mass percentages of Li and Yb in the alloy are Li: 1.10% to 2.00%, Yb 0% to 0.19% and not 0, and the unavoidable impurity content is ⁇ 0.1%.
  • the composition ranges of Li and Yb are Li: 1.35% to 1.70%, and Yb: 0.15% to 0.19%, which can satisfy the good aging strengthening effect of the alloy and is economical.
  • the Yb microalloyed Al-Li alloy provided by the present invention is a Yb microalloyed Al-Mg-Li alloy.
  • Mg, Li, and Yb in the alloy are Mg: 2.70% to 2.80% by mass, and Li: 0.90% to 1.55%, Yb: 0% to 0.17% and not 0, impurity content ⁇ 0.1% is inevitable.
  • the composition ranges of Li and Yb are Mg: 2.70% to 2.80%, Li: 1.10% to 1.35%, and Yb: 0.13% to 0.17%, respectively, to satisfy that the alloy has a good aging strengthening effect and is economical.
  • the Yb microalloyed Al-Li alloy of the present invention Using the Yb microalloyed Al-Li alloy of the present invention, after the alloy is solution treated, single-stage aging at a temperature of 80-180°C for 1h-288h, which has an aging strengthening effect; when the Li content is 1.35%-1.70%, The density of Al-Li alloy is about 2.56 ⁇ 2.53g/cm 3 , the density of Al-Li-Yb alloy is 2.56 ⁇ 2.53g/cm 3 , the density remains basically unchanged, and it can produce good aging strengthening effect.
  • the technical solution of adopting the alloy composition of the present invention not only enables the alloy to obtain a good aging strengthening effect, but also has economy.
  • the Yb microalloyed Al-Mg-Li alloy of the present invention Using the Yb microalloyed Al-Mg-Li alloy of the present invention, after the alloy is solid solution treated, single-stage aging at a corresponding temperature of 80°C to 120°C for 0.25 to 240 hours, which has an aging strengthening effect; the Li content is 1.10% to 1.35 %, the density of Al-Mg-Li alloy is about 2.52 ⁇ 2.55g/cm 3 , the density of Al-Li-Yb alloy is 2.53 ⁇ 2.55g/cm 3 , the density remains basically unchanged, and the effect of strengthening is more obvious .
  • the technical solution adopting the alloy composition of the present invention enables the alloy to produce a good aging strengthening effect and also has production economy.
  • Figure 1 shows the variation curve of the microhardness of Al-1.12Li and Al-1.11Li-0.17Yb alloys with aging time at 80°C;
  • Figure 2 shows the change curve of the microhardness of Al-1.35Li and Al-1.35Li-0.17Yb alloys with aging time at 100°C;
  • Figure 3 shows the change curve of the microhardness of Al-1.70Li and Al-1.67Li-0.17Yb alloys with aging time at 150°C;
  • Figure 4 shows the variation curve of microhardness with aging time of Al-2.00Li and Al-2.00Li-0.17Yb alloys during aging at 180°C;
  • Figure 5 is a comparison diagram of the maximum microhardness of alloys with different compositions and the price
  • Figure 6 shows the change curve of the microhardness with aging time of Al-2.80Mg-0.98Li and Al-2.80Mg-0.90Li-0.15Yb alloy during aging at 80°C;
  • Figure 7 shows the change curve of the microhardness of Al-2.76Mg-1.10Li and Al-2.80Mg-1.10Li-0.15Yb alloys with aging time at 80°C;
  • Figure 8 shows the variation curve of the microhardness with aging time of Al-2.78Mg-1.30Li and Al-2.76Mg-1.35Li-0.15Yb alloy during aging at 120°C;
  • Figure 9 shows the variation curve of microhardness with aging time of Al-2.76Mg-1.55Li and Al-2.76Mg-1.53Li-0.15Yb alloys during aging at 120°C;
  • Fig. 10 is the change curve of hardness increase of Al-Mg-Li alloy after adding element Yb;
  • Figure 11 is the change curve of the alloy cost required for unit hardness increase of Al-Mg-Li and Al-Mg-Li-Yb alloys.
  • the mass percentage of Li and Yb in the alloy is Li: 1.10% ⁇ 2.00%, Yb 0% ⁇ 0.19% and not 0, the inevitable impurity content ⁇ 0.1%, the alloy is 80 ⁇ Single-stage aging at 180°C is 1 ⁇ 288h.
  • Yb microalloyed Al-Mg-Li alloy The mass percentages of Mg, Li and Yb in the alloy are Mg: 2.70% to 2.80%, Li: 0.90% to 1.55%, Yb: 0% to 0.17% and not 0 , Unavoidable impurity content ⁇ 0.1%, single-stage aging of the alloy at 80°C ⁇ 120°C for 0.25 ⁇ 240h.
  • Al-Li-Yb alloy containing Li and Yb in mass percentages of Li: 1.10% to 1.40% and Yb: 0.15% to 0.17%, and an Al-Li alloy with the same Li content as an example. It can be seen from Figure 5 that the cost of Al-Li-Yb alloy has increased by 3.2% compared to Al-Li alloy.
  • the component alloy is preferably aged at 100°C. From the hardness curve in Figure 2, it can be seen that Al-Li-Yb is aged for 168h at 100°C, the alloy hardness can reach 74.5Hv, while the hardness of Al-Li alloy has no obvious change, about 34Hv, and the hardness of Al-Li-Yb alloy is about Al -2.2 times of Li alloy.
  • the alloy of this composition is preferably aged at 150°C.
  • the alloy of this composition is preferably aged at 80°C. According to the hardness curves of Figures 7 and 10, it can be seen that Al-Mg-Li-Yb is aged at 80°C for 240h, and the alloy hardness can reach 87Hv, while the hardness of Al-Mg-Li alloy is comparable to Compared with the solid solution state, there is no significant change.
  • the alloy of this composition is preferably aged at 120°C.
  • the hardness of Al-Mg-Li-Yb alloy is significantly higher than that of Al-Mg-Li The hardness of the alloy.
  • the alloy hardness can reach 102Hv, while Al-Mg-Li alloy aging for 240h, the hardness is about 86Hv, Al-Mg-Li-Yb alloy hardness is about better than Al-Mg -Li alloy has a high hardness of 16Hv. It can be seen from FIG. 11 that, compared with Al-Mg-Li alloy, the alloy cost required for unit hardness increase of Al-Mg-Li-Yb alloy is significantly reduced, about 67% of its cost. While the hardness of the alloy has been significantly improved, the cost performance of the alloy has also been improved.
  • An example is an Al-Li-Yb alloy containing Li and Yb in mass percentages of Li: 1.10% to 1.20% and Yb: 0.15% to 0.17%, and Al-Li with the same Li content.
  • the alloy is preferably aged at 80°C. It can be seen from Fig. 5 that the cost of Al-Li-Yb alloy has increased by 1.3% compared with Al-Li alloy, and it can be seen from Fig. 1 that the hardness of Al-Li-Yb alloy is only higher than that of Al-Li alloy after 48h aging at 80°C. 15Hv.
  • Al-Li-Yb alloy containing Li and Yb in mass percentages of Li: 2.00% to 2.10% and Yb: 0.15% to 0.17%, and Al-Li with the same Li content as an example of the alloy.
  • the alloy is preferably aged at 180°C. It can be seen from Fig. 5 that the cost of Al-Li-Yb alloy has increased by 2.4% compared to Al-Li alloy, and it can be seen from Fig. 4 that the hardness of Al-Li-Yb alloy is only higher than that of Al-Li alloy after aging at 180°C for 48h. Around 5Hv.
  • the alloy is preferably aged at 80°C. It can be seen from Figure 6 and Figure 10 that when aging at 80°C, the Al3Li phase precipitation driving force is too low and the Al3Li phase does not precipitate significantly. Compared with the hardness of the Al-Mg-Li alloy, the hardness of the Al-Mg-Li-Yb alloy is also No significant improvement. It can be seen from Fig. 11 that compared with Al-Mg-Li alloy, the alloy cost required for unit hardness increase of Al-Mg-Li-Yb alloy is lower, but the alloy hardness is not significantly increased.
  • the alloy is preferably aged at 120°C. It can be seen from Fig. 9 and Fig. 10 that after aging at 120°C for 240h, Al3Li phase is dispersed and precipitated, and the hardness of the alloy is significantly improved.
  • the hardness of Al-Mg-Li-Yb alloy is only about 2Hv higher than that of Al-Mg-Li alloy.
  • the Yb microalloyed Al-Li alloy and Al-Mg-Li alloy provided by the present invention can obtain good aging strengthening effects and are economical.
  • the former component is Li: 1.35% to 1.70% by mass percentage, Yb: 0.15% to 0.19%, the unavoidable impurity content is ⁇ 0.1%, the balance is Al;
  • the latter component is Mg: 2.70% to 2.80% by mass percentage, Li: 1.10% to 1.35%, Yb: 0.13% to 0.17%, the inevitable impurity content is ⁇ 0.1%, and the balance is Al.

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Abstract

Yb微合金化的Al-Li和Al-Mg-Li合金。对于Al-Li-Yb合金，各组分含量按质量百分比为：Li 1.11％～2.00％，Yb 0％～0.19％，不可避免杂质含量<0.1％，余量为Al。对于Al-Mg-Li-Yb合金，各组分含量按质量百分比为：Mg 2.70％～2.80％，Li 0.90％～1.55％，Yb 0％～0.17％，不可避免杂质含量<0.1％，余量为Al。对于较低Li含量的合金，通过微量Yb的添加促进Al-Li和Al-Mg-Li合金中Al 3Li相的弥散析出，在密度基本不变的情况下，提高合金的强化效果，降低合金的成本。

Description

Yb微合金化的Al-Li合金 技术领域
本发明涉及Yb微合金化的Al-Li合金，属于合金材料技术领域。
背景技术
铝锂合金在航空航天领域有非常广阔的应用，由于其低密度、高弹性模量、高比强度和疲劳性能优良等特点，使得铝锂合金有非常好的发展和应用前景。由于铝锂合金属于可热处理强化合金，在热处理过程中弥散析出的具有了L12结构的AL3Li亚稳相，其具有非常明显的强化作用。由于Li在铝中的最大固溶度为4.2wt.％,时效过程中可以析出较大体积分数的Al3Li相，使得合金的强度明显提高。
虽然提高Li的含量，可以增加Al3Li相的析出体积分数，但是同时也会带来一些其他问题。由于Li元素化学性质比较活泼，会吸附大量的氢元素，造成合金的氢脆，提高Li的含量也会引起生产成本的提高，此外大量的Al3Li相析出造成的共面滑移也会对合金塑韧性有不利影响。如果降低Li的含量至1.5wt.％，Al3Li相析出驱动力不足，析出困难。
综上，对AL-Li合金进一步的合金化显得尤为重要，研究发现，在Al-Li合金加入微量Sc元素，并通过复杂的双级时效工艺促使合金中析出弥散的L12核壳结构强化相，使得合金进一步提升强化。Al-Mg-Li系列的1420合金是密度最低的铝锂合金，研究人员在1420合金基础加上添加了Sc而成的1421和1423等合金，其力学性能和焊接性能等都有了进一步的提升，并广泛地应用于航空航天领域，但 Sc元素价格昂贵，限制了其工业化应用，而Yb与Sc元素具有类似的性质，都可以析出稳定的具有L12结构的Al3M相，提高合金的强化效果，但Yb元素具有更高的形核率和扩散速率，且Yb元素价格较为便宜，仅为Sc元素的三十分之一。所以本发明将Mg、Li、Yb元素进行复合添加，以期获得低成本且具有良好时效强化效果的合金。
发明内容
本发明的目的在于提供Yb微合金化的Al-Li合金，该合金的生产成本较低且可以产生良好的时效强化效果。
本发明提供的Yb微合金化的Al-Li合金，合金中Li、Yb按质量百分比为Li：1.10％～2.00％，Yb 0％～0.19％且不为0，不可避免杂质含量<0.1％。
优选Li、Yb成分范围分别为Li：1.35％～1.70％，Yb：0.15％～0.19％时，可满足合金良好时效强化效果且兼具经济性。
本发明提供的Yb微合金化的Al-Li合金，是一种Yb微合金化的Al-Mg-Li合金，合金中Mg、Li和Yb按质量百分比为Mg：2.70％～2.80％，Li：0.90％～1.55％，Yb：0％～0.17％且不为0，不可避免杂质含量<0.1％。
优选Li、Yb成分范围分别为Mg：2.70％～2.80％，Li：1.10％～1.35％，Yb：0.13％～0.17％时，可满足合金具有良好的时效强化效果且兼具经济性。
本发明技术方案的优点在于：
采用本发明的Yb微合金化的Al-Li合金，合金经过固溶处理后， 相应的温度80～180℃下单级时效1h～288h，具有时效强化效果；Li含量1.35％～1.70％时，Al-Li合金密度约为2.56～2.53g/cm 3,Al-Li-Yb合金密度为2.56～2.53g/cm 3,密度基本保持不变，且能够产生良好的时效强化效果。采用本发明合金成分的技术方案在使得合金能够得到良好时效强化效果的同时兼具经济性。
采用本发明的Yb微合金化的Al-Mg-Li合金，合金经过固溶处理后，相应的温度80℃～120℃下单级时效0.25～240h，具有时效强化效果；Li含量1.10％～1.35％时，Al-Mg-Li合金的密度约为2.52～2.55g/cm 3,Al-Li-Yb合金密度为2.53～2.55g/cm 3,密度基本保持不变，同时效强化效果更为明显。采用本发明合金成分的技术方案在使得合金能够产生良好的时效强化效果的同时兼具生产经济性。
附图说明
图1为Al-1.12Li、Al-1.11Li-0.17Yb合金在80℃时效过程中显微硬度随时效时间变化曲线；
图2为Al-1.35Li、Al-1.35Li-0.17Yb合金在100℃时效过程中显微硬度随时效时间变化曲线；
图3为Al-1.70Li、Al-1.67Li-0.17Yb合金在150℃时效过程中显微硬度随时效时间变化曲线；
图4为Al-2.00Li、Al-2.00Li-0.17Yb合金在180℃时效过程中显微硬度随时效时间变化曲线；
图5为不同成分合金可达到显微硬度最大值与价格比较图；
图6为Al-2.80Mg-0.98Li、Al-2.80Mg-0.90Li-0.15Yb合金在80℃时效 过程中显微硬度随时效时间变化曲线；
图7为Al-2.76Mg-1.10Li、Al-2.80Mg-1.10Li-0.15Yb合金在80℃时效过程中显微硬度随时效时间变化曲线；
图8为Al-2.78Mg-1.30Li、Al-2.76Mg-1.35Li-0.15Yb合金在120℃时效过程中显微硬度随时效时间变化曲线；
图9为Al-2.76Mg-1.55Li、Al-2.76Mg-1.53Li-0.15Yb合金在120℃时效过程中显微硬度随时效时间变化曲线；
图10为Al-Mg-Li合金添加元素Yb后硬度提升的变化曲线；
图11为Al-Mg-Li与Al-Mg-Li-Yb合金单位硬度提升所需的合金成本的变化曲线。
具体实施方式
下面结合附图及实施例对发明作进一步阐述，但本发明并不限于以下实施例。
Yb微合金化的Al-Li合金，合金中Li、Yb按质量百分比为Li：1.10％～2.00％，Yb 0％～0.19％且不为0，不可避免杂质含量<0.1％，合金在80～180℃下单级时效1～288h。
Yb微合金化的Al-Mg-Li合金，合金中Mg、Li和Yb按质量百分比为Mg：2.70％～2.80％，Li：0.90％～1.55％，Yb：0％～0.17％且不为0，不可避免杂质含量<0.1％，合金在80℃～120℃下单级时效0.25～240h。
实施例1
以含有Li、Yb成分质量百分比分别为Li：1.10％～1.40％，Yb： 0.15％～0.17％的Al-Li-Yb合金及相同Li含量的Al-Li合金为例。由图5可知，Al-Li-Yb合金相比Al-Li合金成本增加了3.2％。该成分合金优选在100℃时效。由图2硬度曲线可知Al-Li-Yb在100℃下时效168h，合金硬度可达到74.5Hv，而Al-Li合金硬度没有明显的变化，约为34Hv，Al-Li-Yb合金硬度约为Al-Li合金的2.2倍。
实施例2
以含有Li、Yb成分质量百分比分别为Li：1.60％～1.70％，Yb：0.15％～0.17％的Al-Li-Yb合金及相同Li含量Al-Li合金为例。由图5可知，Al-Li-Yb合金相比Al-Li合金成本增加了0.9％.该成分合金优选150℃下时效。由图3硬度曲线可知Al-Li-Yb在150℃下时效24h-72h，合金硬度可达到92Hv，而Al-Li合金硬度没有明显的变化，约为36Hv，Al-Li-Yb合金硬度约为Al-Li合金的2.6倍。
实施例3
以含有Mg、Li、Yb成分质量百分比分别为Mg：2.75±0.05，Li：1.10±0.05，Yb：0.15±0.02的Al-Mg-Li-Yb合金及相同Li含量的Al-Mg-Li合金为例。该成分合金优选在80℃时效，由图7和图10的硬度曲线可知Al-Mg-Li-Yb在80℃下时效240h，合金硬度可达到87Hv，而Al-Mg-Li合金硬度与相比固溶态相比没有明显变化，由于Yb促进了Al3Li相的析出，因此Al-Mg-Li-Yb合金硬度有了明显提高，约比Al-Mg-Li合金硬度高26Hv。由图11可知，从合金成本与时效后合金硬度提高值的比值来看，即提升单位硬度所需合金成本，其Al-Mg-Li-Yb合金的单位硬度提升所需合金成本大幅降低，约为 Al-Mg-Li合金的8％，性价比大幅提高。
实施例4
以含有Mg、Li、Yb成分质量百分比分别为Mg：2.75±0.05，Li：1.35±0.05，Yb：0.15±0.02的Al-Mg-Li-Yb合金及相同Li含量的Al-Mg-Li合金为例。该成分合金优选在120℃时效，由图8和图10硬度曲线可知，时效初期，由于Yb对Al3Li相析出的促进作用，Al-Mg-Li-Yb合金的硬度明显高于Al-Mg-Li合金的硬度。Al-Mg-Li-Yb在120℃下时效192h，合金硬度可达到102Hv，而Al-Mg-Li合金时效240h后，硬度约为86Hv，Al-Mg-Li-Yb合金硬度约比Al-Mg-Li合金硬度高16Hv。由图11可知，相比于Al-Mg-Li合金，Al-Mg-Li-Yb合金的单位硬度提升所需合金成本明显降低，约为其成本的67％。合金硬度得到明显提升的同时，合金的性价比也有一定提高。
对比例1
以含有Li、Yb成分质量百分比分别为Li：1.10％～1.20％，Yb：0.15％～0.17％的Al-Li-Yb合金及相同Li含量Al-Li为合金例。该合金优选80℃时效。由图5可知，Al-Li-Yb合金相比Al-Li合金成本增加了1.3％，并由图1可知在80℃下时效48h，Al-Li-Yb合金硬度仅仅比Al-Li合金硬度高15Hv。
对比例2
以含有Li、Yb成分质量百分比分别为Li：2.00％～2.10％，Yb：0.15％～0.17％的Al-Li-Yb合金及相同Li含量Al-Li为合金例。该合金 优选在180℃时效。由图5可知，Al-Li-Yb合金相比Al-Li合金成本增加了2.4％，并由图4可知在180℃下时效48h，Al-Li-Yb合金硬度仅仅比Al-Li合金硬度高5Hv左右。
对比例3
以含有Mg、Li、Yb成分质量百分比分别为Mg：2.75±0.05，Li：0.95±0.05，Yb：0.15±0.02的Al-Mg-Li-Yb合金及相同Li含量Al-Mg-Li为合金例。该合金优选80℃时效。由图6和图10可知在80℃下时效，由于Al3Li相的析出驱动力太低，Al3Li相没有明显析出，相比于Al-Mg-Li合金硬度，Al-Mg-Li-Yb合金硬度也没有明显提高。由图11可知，相比Al-Mg-Li合金，Al-Mg-Li-Yb合金的单位硬度提升所需合金成本较低，但合金硬度没有明显提升。
对比例4
以含有Mg、Li、Yb成分质量百分比分别为Mg：2.75±0.05，Li：1.55±0.05，Yb：0.15±0.02的Al-Mg-Li-Yb合金及相同Li含量Al-Mg-Li为合金例。该合金优选在120℃时效。由图9和图10可知在120℃下时效240h，Al3Li相弥散析出，合金的硬度都得到明显提升，Al-Mg-Li-Yb合金硬度仅仅比Al-Mg-Li合金硬度高2Hv左右，这是由于在Li含量较高的情况下，由于Al3Li相的析出驱动力足够大，不需Yb的促进作用，Al3Li相亦可大量析出，使合金得到强化。由图11可知，相比Al-Mg-Li合金，Al-Mg-Li-Yb合金的单位硬度提升所需合金成本没有明显降低，添加合金元素Yb后，性价比并没有得到提高。
综合以上分析，本发明提供的Yb微合金化的Al-Li合金和Al-Mg-Li合金，能够得到良好的时效强化效果且兼具经济性。前者成分按质量百分比为Li：1.35％～1.70％，Yb：0.15％～0.19％，不可避免杂质含量<0.1％,余量为Al；后者成分按质量百分比为Mg：2.70％～2.80％，Li：1.10％～1.35％，Yb：0.13％～0.17％，不可避免杂质含量<0.1％，余量为Al。

Claims (5)

  1. Yb微合金化的Al-Li合金，其特征在于，合金中Li、Yb按质量百分比为Li：1.10％～2.00％，Yb 0％～0.19％且不为0，不可避免杂质含量<0.1％。
  2. 按照权利要求1所述的Yb微合金化的Al-Li合金，其特征在于，Li、Yb成分范围分别为Li：1.35％～1.70％，Yb：0.15％～0.19％。
  3. Yb微合金化的Al-Li合金，其特征在于，是一种Yb微合金化的Al-Mg-Li合金，合金中Mg、Li、Yb按质量百分比为Mg：2.70％～2.80％，Li：0.90％～1.55％，Yb：0％～0.17％且不为0，不可避免杂质含量<0.1％。
  4. 按照权利要求3所述的Yb微合金化的Al-Li合金，其特征在于，Mg、Li、Yb成分范围分别为Mg：2.70％～2.80％，Li：1.10％～1.35％，Yb：0.13％～0.17％。
  5. 按照权利要求1～4所述的Yb微合金化的Al-Li合金，对于Al-(1.35～1.70)Li合金和Al-(2.70～2.80)Mg-(1.10～1.35)Li合金，Yb的添加带来其力学性能的显著提高。
PCT/CN2020/075645 2019-02-22 2020-02-18 Yb微合金化的AI-Li合金 Ceased WO2020169014A1 (zh)

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20110041963A1 (en) * 2008-04-18 2011-02-24 United Technologies Corporation Heat treatable l12 aluminum alloys
WO2014159324A1 (en) * 2013-03-14 2014-10-02 Alcoa Inc. Improved aluminum-magnesium-lithium alloys, and methods for producing the same
CN107190219A (zh) * 2017-04-07 2017-09-22 上海交通大学 含镁铸造铝锂合金的热处理方法
CN109811205A (zh) * 2019-02-22 2019-05-28 北京工业大学 一种Yb微合金化的Al-Li合金
CN109881129A (zh) * 2019-03-14 2019-06-14 北京工业大学 一种Al-Li-Yb合金时效处理工艺
CN110438376A (zh) * 2019-08-13 2019-11-12 北京工业大学 一种Yb微合金化的Al-Mg-Li合金

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20110041963A1 (en) * 2008-04-18 2011-02-24 United Technologies Corporation Heat treatable l12 aluminum alloys
WO2014159324A1 (en) * 2013-03-14 2014-10-02 Alcoa Inc. Improved aluminum-magnesium-lithium alloys, and methods for producing the same
CN107190219A (zh) * 2017-04-07 2017-09-22 上海交通大学 含镁铸造铝锂合金的热处理方法
CN109811205A (zh) * 2019-02-22 2019-05-28 北京工业大学 一种Yb微合金化的Al-Li合金
CN109881129A (zh) * 2019-03-14 2019-06-14 北京工业大学 一种Al-Li-Yb合金时效处理工艺
CN110438376A (zh) * 2019-08-13 2019-11-12 北京工业大学 一种Yb微合金化的Al-Mg-Li合金

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